High-strength steel sheet having excellent ductility and low-temperature toughness and method for manufacturing thereof

ABSTRACT

The present invention relates to a structural steel sheet suitable for ships or steel structures and, more particularly, to a high-strength steel sheet having excellent ductility and low-temperature toughness and a method for manufacturing same.

TECHNICAL FIELD

The present disclosure relates to a structural steel sheet suitable for ships or steel structures and, more particularly, to a high-strength steel sheet having excellent ductility and low-temperature toughness and a method for manufacturing the same.

BACKGROUND ART

A ship, a steel structure, or the like may experience accidents such as flooding or sinking as a steel plate is fractured by external impacts such as a collision. In addition, cracks may occur due to forming processes during the manufacture of the ship or steel structure. In this case, there may be a problem such as the increase in a construction period or manufacturing costs.

In order to solve the above problems, it is necessary to increase an elongation while maintaining the strength of the steel sheet used in ships or steel structures at the required level. The higher the elongation of the steel, the more deformation may be accommodated until the steel is fractured even if the steel is deformed due to the external impacts, etc., so that the occurrence of fracture may be suppressed and the possibility of the occurrence of cracks due to processing may be reduced.

In general, since the strength and elongation of steel have an inverse relationship, it is very hard to increase the elongation while maintaining the strength. Nevertheless, the following technologies have been developed.

For example, Patent Document 1 discloses a steel plate having excellent collision absorption property while having a tensile strength of 490 MPa or more and a uniform elongation of 15% or more by controlling an average grain diameter of ferrite as a main phase between 3 and 12 jam and making the ferrite fraction 90% or more while refining an average equivalent circle diameter of a second phase to 0.8 μm or less.

Patent Document 2 discloses a steel sheet having a microstructure made of ferrite and a hard second phase, a volume fraction of the ferrite of 75% or more over the entire sheet thickness, a hardness of Hv 140 or more and 160 or less, and an average crystal grain size of 2 μm or more by applying a process including front ooling, air cooling, and rear ooling after rolling.

In addition, Patent Document 3 discloses a thick steel plate in which a microstructure is mainly composed of ferrite and pearlite in order to increase energy absorption capability during a collision, and an average dislocation density of the ferrite is lowered to a certain level or less while a hardness, a fraction, an average area, and an average circumferential length of the phase satisfying certain conditions. Further, in order to obtain the above-described thick steel plate, a process of heating a steel material to the temperature higher than a normal reheating temperature, and then performing controlled rolling on the steel material and air cooling or weak water cooling on the rolled steel material is disclosed.

However, it may be found that the above-described techniques have several problems.

Specifically, although the fracture of the steel plate is more related to total elongation (or fracture elongation) than uniform elongation, Patent Document 1 discloses only uniform elongation, and but does not substantially disclose the effect of suppressing defects such as the fracture due to external impacts or the like. Patent Document 2 also discloses only the uniform elongation, and therefore, the total elongation or the like of the steel plate disclosed in Patent Document 2 is unclear. On the other hand, Patent Document 3 discloses the total elongation, but does not disclose securing the toughness at all, which is a very important property of the structural steel sheet.

In other words, it is important to secure not only strength and ductility (total elongation), but also toughness, in particular, low-temperature toughness, as properties required for the structural steel sheet suitable for use in ships, steel structures, or the like. Accordingly, it is necessary to develop a structural steel sheet having all of these properties.

(Patent Document 1) Korean Patent Laid-open Publication No. 10-2006-0127762

(Patent Document 2) Korean Patent Laid-open Publication No. 10-2016-0104077

(Patent Document 3) Japanese Patent No. 5994819

DISCLOSURE Technical Problem

An aspect of the present disclosure is to provide a high-strength steel sheet having excellent ductility and low-temperature toughness and a method for manufacturing the same in providing a steel sheet suitable for a structural use.

An object of the present disclosure is not limited to the abovementioned contents. Those skilled in the art will have no difficulty in understanding an additional object of the present disclosure from the general contents of the present specification.

Technical Solution

According to an aspect of the present disclosure, a high-strength steel sheet having excellent ductility and low-temperature toughness contains: by wt %, 0.05 to 0.12% of carbon (C), 0.2 to 0.5% of silicon (Si), 1.2 to 1.8% of manganese (Mn), 0.012% or less of phosphorus (P), 0.005% or less of sulfur (S), 0.01 to 0.06% of aluminum (Al), 0.005 to 0.02% of titanium (Ti), 0.01 to 0.03% of niobium (Nb), 0.002 to 0.006% of nitrogen (N), 0.5% or less of nickel (Ni), the balance Fe, and inevitable impurities,

in which the steel contains polygonal ferrite having an average grain size (equivalent circle diameter) of 2 to 8 μm as a main phase and pearlite and bainite as a second phase in a microstructure, and has a thickness of 8 to 15 mm.

According to another aspect of the present disclosure, a method for manufacturing a steel sheet having excellent ductility and low-temperature toughness includes: heating a steel slab satisfying the above-described alloy composition in a temperature range of 1100 to 1200° C.; manufacturing the heated steel slab into a hot-rolled steel plate by rough rolling and finish rolling the heated steel slab; and cooling the hot-rolled steel plate, in which the finish rolling is performed in a temperature range of Ar3+70° C. to Ar3+170° C.

Advantageous Effects

As set forth above, it is possible to provide a steel sheet having excellent low-temperature toughness as well as high strength and high ductility.

In addition, the steel sheet of the present disclosure has an effect that may be advantageously applied as a structural steel sheet.

BEST MODE FOR INVENTION

In general, as the strength of steel increases, the ductility of the steel is relatively reduced. Accordingly, it is not easy to manufacture steel having high strength and excellent elongation. In addition, the high elongation of steel does not necessarily mean that the steel has excellent low-temperature toughness, so it is more difficult to secure excellent low-temperature toughness as well as high strength and high ductility.

However, as the present inventors have deeply researched the development of a steel sheet capable of securing the low-temperature toughness as well as the high strength and high ductility, the present inventors found that it is possible to provide a steel sheet having target mechanical properties by defining alloy compositions and manufacturing conditions as follows, and reached the completion of the present disclosure.

Hereinafter, the present disclosure will be described in detail.

According to an aspect of the present disclosure, a high-strength steel sheet having excellent ductility and low-temperature toughness may contain, by wt %, 0.05 to 0.12% of carbon (C), 0.2 to 0.5% of silicon (Si), 1.2 to 1.8% of manganese (Mn), 0.012% or less of phosphorus (P), 0.005% or less of sulfur (S), 0.01 to 0.06% of aluminum (Al), 0.005 to 0.02% of titanium (Ti), 0.01 to 0.03% of niobium (Nb), 0.002 to 0.006% of nitrogen (N), and 0.5% or less of nickel (Ni).

Hereinafter, the reason for limiting the alloy compositions of the steel sheet provided by the present disclosure as described above will be described in detail.

On the other hand, unless specifically stated in the present disclosure, the content of each element is based on a weight, and the fraction of a microstructure is based on an area.

Carbon (C): 0.05 to 0.12%

Carbon (C) is an element that affects the fraction of pearlite in a steel microstructure, and is advantageous in securing strength. In order to secure a target level of strength in the present disclosure, the carbon (C) may be contained in an amount of 0.05% or more. In particular, in a series of processes (rolling and cooling processes) for manufacturing the steel sheet of the present disclosure, it is preferable to contain C in an amount of 0.05% or more. However, when the content exceeds 0.12%, the fraction of the pearlite in the steel microstructure becomes excessive, so low-temperature toughness decreases.

Therefore, in the present disclosure, C may be contained in an amount of 0.05 to 0.12%, and more advantageously, may be contained in an amount of 0.06 to 0.10%.

Silicon (Si): 0.2 to 0.5%

Silicon (Si) is an element that helps deoxidation of steel, increases hardenability, and may be contained in an amount of 0.2% or more in order to secure a target level of strength. However, when the content exceeds 0.5%, there is a problem that the strength is excessively increased, thereby impairing total elongation and low-temperature impact toughness.

Therefore, in the present disclosure, Si may be contained in an amount of 0.2 to 0.5%.

Manganese (Mn): 1.2 to 1.8%

Manganese (Mn) is an element that is useful for increasing the strength without significantly reducing the elongation of the steel. In order to secure the target level of strength in the present disclosure, Mn may be contained in an amount of 1.2% or more, but when the content exceeds 1.8%, the strength of the steel increases significantly, thereby making it difficult to secure ductility.

Therefore, in the present disclosure, Mn may be contained in an amount of 1.2 to 1.8%, and more advantageously, may be contained in an amount of 1.4 to 1.7%.

Phosphorus (P): 0.012% or less

Phosphorus (P) is an impurity that is inevitably mixed in steel, and needs to be minimized because the phosphorus (P) reduces the ductility and low-temperature impact toughness of the steel. In the present disclosure, even if P is contained in an amount of 0.012% or less, since there is no great difficulty in securing the intended physical properties, an upper limit of P may be limited to 0.012%. However, 0% may be excluded in consideration of a load during a process of manufacturing steel.

Sulfur (S): 0.005% or less

Sulfur (S) is an impurity that is inevitably mixed in steel, such as P, and is necessary to minimize its content since the sulfur (S) forms sulfides and significantly reduces ductility. In the present disclosure, even if S is contained in an amount of 0.005% or less, since there is no great difficulty in securing the intended physical properties, an upper limit of S may be limited to 0.005%. However, 0% may be excluded in consideration of a load during the process of manufacturing steel.

Aluminum (Al): 0.01 to 0.06%

Aluminum (Al) is an essential element for deoxidation of steel, and may be contained in an amount of 0.01% or more in order to secure cleanliness of the steel. However, when the content is excessive, since the toughness of a welded joint may be impaired, the content may be limited to 0.06% or less in consideration of the impairment of the toughness.

Titanium (Ti): 0.005 to 0.02%

Titanium (Ti) is an element useful for refining grains of ferrite during austenite-ferrite transformation by suppressing excessive growth of austenite during a heating process in the process of manufacturing steel. In order to sufficiently obtain the above-described effects, Ti may be contained in an amount of 0.005% or more, but when the content exceeds 0.02%, coarse nitrides are formed, thereby reducing the effect of grain refinement and deteriorating impact toughness.

Therefore, in the present disclosure, Ti may be contained in an amount of 0.005 to 0.02%.

Niobium (Nb): 0.01 to 0.03%

Niobium (Nb) is effective in refining grains of austenite by being precipitated as carbonitride during a rolling process in the process of manufacturing steel, and contributes to the improvement in the strength. In order to sufficiently obtain such an effect, Nb may be added in an amount of 0.01% or more, but when the content exceeds 0.03%, the strength excessively increases, thereby making it difficult to secure the ductility and impairing the toughness of a welded joint.

Therefore, in the present disclosure, Nb may be contained in an amount of 0.01 to 0.03%.

Nitrogen (N): 0.002 to 0.006%

Nitrogen (N) is advantageous in obtaining an effect of suppressing the growth of the grains of the austenite during the heating of the steel by being combined with the Ti, Nb, or the like and refining grains by forming fine carbonitrides during the rolling. To this end, N may be added in an amount of 0.002% or more, but when the content exceeds 0.006%, the surface quality of steel cast and sheet may be deteriorated.

Therefore, in the present disclosure, N may be contained in an amount of 0.002 to 0.006%.

Nickel (Ni): 0.5% or less (including 0%)

Nickel (Ni) is an element that does not significantly impair the elongation while improving strength by refining grains of ferrite, similar to the Mn. By adding such Ni in a certain amount, the strength, ductility, and low-temperature toughness targeted in the present disclosure may be more advantageously secured. However, when the content exceeds 0.5%, the elongation decreases and the manufacturing cost increases, so Ni may be contained in an amount of 0.5% or less.

In the present disclosure, even if Ni is not added, it is not unreasonable to secure physical properties, and Ni may be 0%.

The remaining component of the present disclosure is iron (Fe). However, in a general manufacturing process, unintended impurities may inevitably be mixed from a raw material or the surrounding environment, and thus, these impurities may not be excluded. Since these impurities are known to anyone with ordinary skill in the manufacturing process, all the contents are not specifically mentioned in the present specification.

The steel sheet of the present disclosure having the above-described alloy compositions may contain polygonal ferrite as a main phase and pearlite and bainite as a second phase in a microstructure.

When the microstructure of the steel sheet as in the present disclosure is a single phase of ferrite, an average grain size (grain diameter) of the ferrite needs to be very small in order to secure the strength targeted in the present disclosure. In this case, the uniform elongation of the steel is significantly reduced, so it becomes impossible to achieve the target level of total elongation. In addition, even when the microstructure is made of a single phase of acicular ferrite or bainite, the strength is excellent, but it is difficult to secure high ductility.

In addition, even when the ferrite is the main phase and the second phase is a hard phase (bainite or martensite), while the uniform elongation is excellent, post elongation indicating the ductility after necking is inferior, thereby making it difficult to secure the total elongation.

Accordingly, the present disclosure may form a ferrite-pearlite microstructure of the steel sheet in order to secure a balance between the strength and ductility of the steel sheet, and secure the intended physical properties by minimizing the fraction of the bainite which may be partially contained during the process of manufacturing a steel sheet.

In particular, in the second phase, the pearlite is preferably contained in an area fraction of 5 to 25%, and the bainite is preferably contained in an area fraction of 2% or less (including 0%). Specifically, when the fraction of the pearlite is less than 5%, it is difficult to secure the target level of strength, and when the fraction exceeds 25%, the elongation decreases and the target level of toughness may not be achieved. On the other hand, when the fraction of the bainite exceeds 2%, the post elongation is lowered, and thus it is difficult to secure the target level of total elongation in the present disclosure.

On the other hand, the smaller the average grain size (equivalent circle diameter) of the polygonal ferrite, the more advantageous it is to improve the strength and low-temperature toughness of the steel, while the elongation decreases, so it is necessary to properly control the average grain size of the polygonal ferrite.

The relationship between the average grain size and elongation of the polygonal ferrite is not linear, and when the average grain size of the polygonal ferrite is smaller than 2 μm, the elongation tends to decrease rapidly.

In the present disclosure, by controlling the average grain size of the polygonal ferrite to 2 to 8 μm, it is possible to secure the balance between the strength and ductility from appropriate refinement. When the average grain size of the polygonal ferrite is less than 2 μm, the uniform elongation is significantly reduced, thereby making it difficult to secure the total elongation. On the other hand, when the size exceeds 8 μm, the fraction of the pearlite should be increased to secure the target level of strength, but the low-temperature impact toughness is deteriorated.

More specifically, the steel sheet of the present disclosure having a microstructure as described above has a yield strength of 355 MPa or more, a tensile strength of 490 MPa or more, an elongation of 30% or more, and an impact toughness of 100 J or more at −40° C., and therefore, may secure the low-temperature toughness as well as the strength and ductility.

The steel sheet of the present disclosure may have a thickness of 8 to 15 mm.

Hereinafter, a method for manufacturing high-strength steel sheet having excellent ductility and low-temperature toughness according to another aspect of the present disclosure will be described in detail.

The high-strength steel sheet according to the present disclosure may be manufactured through a series of processes of [heating-hot rolling-cooling] a steel slab that satisfies the alloy compositions proposed in the present disclosure.

Hereinafter, each of the above process conditions will be described in detail.

Heating Steel Slab

In the present disclosure, the steel slab may be preferably subjected to the heating to homogenizing followed by the hot rolling. In this case, the heating process is preferably performed at 1100 to 1200° C.

When the heating temperature is less than 1100° C., the steel slab is not sufficiently uniform, and Nb carbonitride or the like present in the center of the thickness of the steel slab is not sufficiently dissolved, thereby making it difficult to secure the target level of strength. On the other hand, when the temperature exceeds 1200° C., the elongation and low-temperature toughness are degraded due to the abnormal grain growth of the grains of the austenite, which is not preferable.

In performing the heating in the above-described temperature range, the heating time may be set differently according to the thickness of the steel slab, and it is preferable to set it so that the steel slab may be sufficiently uniform from the surface to the center of the thickness of the steel slab. Usually, heating may be performed for 1 minute or more per 1 mm of the thickness of the steel slab.

Hot Rolling

The hot-rolled steel plate may be manufactured by hot rolling the heated steel slab according to the above. In this case, the two-step rolling may be performed.

Specifically, the rough rolling is performed in the first rolling, which may be performed immediately after the extraction of the heated steel slab from the heating furnace. The rough rolling may include broadside rolling to secure the width of the final steel plate, and the rolling may be carried out up to the thickness at which the finish rolling, which is the subsequent second rolling, begins.

As mentioned above, the finish rolling is performed as the second rolling, and the rolling may be performed so as to have an intended thickness. In the present disclosure, it is preferable to perform the finish rolling in a temperature range of Ar3+70° C. to Ar3+170° C.

In general, the lower the temperature during the finish rolling, the smaller the grain size of the ferrite in the final microstructure, so that the strength and low-temperature toughness may be improved and the elongation may be reduced.

Therefore, in order to simultaneously improve the ductility as well as the strength and low-temperature toughness targeted in the present disclosure, the finish rolling needs to be performed in an appropriate temperature range. But the temperature range may be very narrow, in this case, there is a problem that it is difficult to industrially manufacture the steel sheet.

Accordingly, as the present inventors have deeply studied the relationship between the alloy compositions and the manufacturing process, the present inventors found that it is possible to expand the temperature range advantageous for securing the intended physical properties during the finish rolling by appropriately adding Mn or Mn and Ni in the alloy compositions.

Specifically, the Mn and Ni lower the ferrite transformation temperature to induce the ferrite grain refinement, thereby improving the strength and low-temperature toughness and not significantly impairing the elongation.

As a result, by performing the finish rolling the steel with the content of Mn and Ni proposed in the present disclosure in a temperature range of Ar3+70° C. to Ar3+170° C., the steel sheet having excellent strength and ductility as well as low-temperature toughness may be obtained.

When the temperature during the finish rolling is less than Ar3+70° C., the strength of the steel increases rapidly and the elongation decreases significantly. On the other hand, when the temperature exceeds Ar3+170° C., the austenite becomes coarse and the grains of the ferrite in the final microstructure, become coarse, so there is a problem that the strength and low-temperature toughness are lowered.

Here, Ar3 may be represented by the following formula.

[Ar3=910−310C−80Mn−20Cu−55Ni−15Cr−80Mo (each element is represented by weight percent)]

In addition, it is preferable to perform the finish rolling such that the cumulative reduction ratio is 60 to 90% during the finish rolling in the above-described temperature range. When the cumulative reduction ratio during the finish rolling is less than 60%, the average grain size of the ferrite becomes coarse, and thus, it is difficult to secure the strength of the target level, whereas when the cumulative reduction ratio exceeds 90%, the average grain size of the ferrite becomes too fine, and thus, it is advantageous for securing strength but the elongation is deteriorated.

Cooling

As described above, the hot-rolled steel plate manufactured by performing the hot rolling may be cooled. In this case, it is preferable to perform cooling to room temperature through air cooling, which means cooling in the atmosphere.

When water cooling is applied during the above cooling, the ferrite is excessively refined or the fraction of a hard phase such as the bainite as the second phase increases, and thus, the probability of cooling unevenness increases and it is difficult to secure the post elongation, so there is a problem that it becomes difficult to secure the total elongation.

The steel sheet of the present disclosure manufactured through the series of manufacturing processes described above has a thickness of 8 to 15 mm, and the microstructure intended in the present disclosure may be uniformly formed, regardless of any thickness within the thickness range.

Hereinafter, the present disclosure will be described in more detail through embodiments. It should be noted that the following examples are for describing exemplary examples of the present disclosure, and the scope of the present disclosure is not limited by the following examples. This is because the scope of the present disclosure is determined by matters described in the claims and matters reasonably inferred therefrom.

[Mode for Invention]

(Inventive Example)

After preparing molten steel having the alloy compositions shown in Table 1, the steel slab having a thickness of 250 mm was obtained by a continuous casting method. Thereafter, a steel plate having a thickness of 8 to 15 mm was manufactured through heating, rolling, and cooling under the conditions shown in Table 2 below. When it comes to cooling, air and water cooling were applied, and in the case of the water cooling, the cooling was performed at a cooling rate of about 20° C./s, the water cooling was terminated at 650° C., and then the air cooling was performed to room temperature.

TABLE 1 Steel Alloy Composition (wt %) No. C Si Mn P S Al Ti Nb N Ni Ar3 1 0.11 0.23 1.34 0.008 0.003 0.035 0.014 0.022 0.003 0 769 2 0.09 0.28 1.47 0.011 0.002 0.023 0.012 0.026 0.004 0 765 3 0.08 0.34 1.53 0.007 0.004 0.019 0.013 0.021 0.003 0.13 756 4 0.08 0.25 1.34 0.007 0.003 0.041 0.016 0.014 0.005 0.45 753 5 0.07 0.42 1.63 0.009 0.004 0.031 0.008 0.026 0.003 0 758 6 0.05 0.39 1.74 0.008 0.002 0.033 0.009 0.026 0.003 0 755 7 0.14 0.25 1.35 0.007 0.003 0.038 0.012 0.021 0.004 0 759 8 0.04 0.36 1.65 0.009 0.003 0.025 0.013 0.027 0.003 0 766 9 0.08 0.41 1.58 0.009 0.004 0.048 0.002 0.018 0.005 0 759 10 0.09 0.29 1.45 0.011 0.003 0.036 0.012 0.003 0.004 0 766

TABLE 2 Finish Finish Heating Rolling Rolling Thick- Temper- Temper- Cumulative Steel ness ature ature Reduction No. (mm) (° C.) (° C.) Ratio (%) Cooling Division 1 15 1124 893 70 Air Inventive Cooling Example 1 2 15 1135 903 80 Air Inventive Cooling Example 2 3 15 1108 881 80 Air Inventive Cooling Example 3 4 15 1123 854 85 Air Inventive Cooling Example 4 5 15 1143 884 80 Air Inventive Cooling Example 5 6 15 1155 843 75 Air Inventive Cooling Example 6 2 11 1172 881 80 Air Inventive Cooling Example 7 3 11 1149 865 80 Air Inventive Cooling Example 8 4 11 1155 853 70 Air Inventive Cooling Example 9 5 8 1189 892 70 Air Inventive Cooling Example 10 6 8 1194 913 80 Air Inventive Cooling Example 11 7 15 1243 909 80 Air Comparative Cooling Example 1 8 15 1133 892 75 Air Comparative Cooling Example 2 9 15 1119 845 85 Water Comparative Cooling Example 3 10 15 1129 841 50 Water Comparative Cooling Example 4 5 15 1134 852 80 Water Comparative Cooling Example 5 3 15 1116 804 80 Air Comparative Cooling Example 6 1 15 1125 979 70 Air Comparative Cooling Example 7 6 23 1132 867 85 Air Comparative Cooling Example 8

In order to observe the microstructure of each steel plate manufactured as described above, after a specimen was cut at the quarter of of the thickness of each steel plate, polished and etched with a nital etching solution, the specimen was observed with an optical microscope. Thereafter, the average grain size (equivalent circle diameter) of polygonal ferrite, the fraction of pearlite, and the fraction of bainite were measured using an image analyzer connected to an optical microscope, and the results are shown in Table 3 below. In this case, the fractions of the pearlite and bainite were measured based on the area thereof.

In addition, tensile specimens and impact specimens were cut at the quarter of the width of each steel plate and mechanical properties thereof were evaluated, and the results are shown in Table 3 below.

In this case, the tensile specimen was machined into a proportional specimen with a gauge length of 5.65×√ (specimen width×specimen thickness) by setting a specimen width to 25 mm and setting the thickness of the specimen to the thickness of the steel plate such that the specimen length was perpendicular to the rolling direction of the steel sheet, and the yield strength (YS), tensile strength (TS), and total elongation (E1) values were measured through a room temperature tensile test.

In addition, the impact specimen was machined into an ASTM E 23 Type A standard specimen (however, a steel plate with a thickness of 8 mm was machinedinto subsize specimens (10 mm×7.5 mm)) such that the length of the specimen was perpendicular to the rolling direction of the steel plate, and then subjected to an impact test at −40° C., which was represented as the average of the energy values measured from three specimens.

TABLE 3 Microstructure Mechanical Physical Property Frac- Aver- tion Frac- age of tion Total Impact Grain Pearl- of Elon- Tough- Size of ite Bainite Yield Tensile ga- ness Ferrite (area (area Strength Strength tion (−40° Division (μm) %) %) (MPa) (MPa) (%) C., J) Inventive 7.2 22 1 374 537 33 211 Example 1 Inventive 7.8 17 1 367 521 35 179 Example 2 Inventive 5.5 15 0 398 523 37 311 Example 3 Inventive 4.7 14 0 382 518 35 327 Example 4 Inventive 6.1 10 1 375 519 36 336 Example 5 Inventive 4.4  6 0 402 511 38 385 Example 6 Inventive 3.8 18 0 385 521 33 299 Example 7 Inventive 2.6 16 0 419 520 36 312 Example 8 Inventive 2.8 14 0 423 528 35 325 Example 9 Inventive 2.1 19 1 432 526 35 124 Example 10 Inventive 2.3 16 2 416 531 34 132 Example 11 Compara- 10.2  29 1 391 569 28  75 tive Example 1 Compara- 7.2  4 0 367 481 34 259 tive Example 2 Compara- 6.3  6 14  425 563 28 277 tive Example 3 Compara- 8.8  7 18  413 565 27  84 tive Example 4 Compara- 4.7  3 21  444 552 29 247 tive Example 5 Compara- 1.7 16 0 489 548 29 297 tive Example 6 Compara- 9.9 20 0 350 506 35 141 tive Example 7 Compara- 9.5 14 1 352 486 34 192 tive Example 8

(In Table 3, except for the fractions of pearlite and bainite, the remainder is polygonal ferrite.)

As shown in Tables 1 to 3, Inventive Examples 1 to 11 satisfying all of the alloy compositions and manufacturing conditions proposed in the present disclosure may be confirmed that all of the strength, ductility, and low-temperature toughness are secured above the target level.

On the other hand, in Comparative Example 1 in which the content of C in the alloy compositions was excessive and the temperature when heating the slab was too high, the fraction of the pearlite was high, and the average grain size of the ferrite was coarse, so the elongation and impact energy value were inferior. In addition, Comparative Example 2 in which the content of C in the alloy compositions was insufficient was not able to secure the target level of strength due to the low fraction of pearlite.

On the other hand, in Comparative Examples 3 to 5 in which water cooling was applied during the cooling after the hot rolling, the bainite phase was excessively formed and the strength was high, while the elongation was inferior to less than 30%. Among these, it may be seen that in the case of Comparative Example 4 where the cumulative reduction ratio is insufficient during the finish rolling, the low-temperature toughness was also inferior.

Comparative Examples 6 and 7, respectively, correspond to the case where the finish hot rolling temperature deviated from the present disclosure. In Comparative Example 6, the ferrite particle diameter was too small, so the strength was high, but the ductility was inferior. On the other hand, in Comparative Example 7, the ferrite particle diameter was too large, so the strength did not reach the target level.

In Comparative Example 8, the thickness of the final steel plate was 23 mm, and the air cooling was applied after the hot rolling, but the air cooling rate was relatively slow, so that the strength of the target level could not be secured. 

1. A high-strength steel sheet having excellent ductility and low-temperature toughness, comprising: by wt %, 0.05 to 0.12% of carbon (C), 0.2 to 0.5% of silicon (Si), 1.2 to 1.8% of manganese (Mn), 0.012% or less of phosphorus (P), 0.005% or less of sulfur (S), 0.01 to 0.06% of aluminum (Al), 0.005 to 0.02% of titanium (Ti), 0.01 to 0.03% of niobium (Nb), 0.002 to 0.006% of nitrogen (N), 0.5% or less of nickel (Ni), the balance Fe, and inevitable impurities, wherein the steel comprises polygonal ferrite having an average grain size (circle equivalent diameter) of 2 to 8 μm as a main phase and pearlite and bainite as a second phase in a microstructure, and has a thickness of 8 to 15 mm.
 2. The high-strength steel sheet of claim 1, wherein in the second phase, the pearlite is contained in an area fraction of 5 to 25%, and the bainite is contained in an area fraction of 2% or less (including 0%).
 3. The high-strength steel sheet of claim 1, wherein the steel sheet has a yield strength of 355 MPa or more, a tensile strength of 490 MPa or more, and an elongation of 30% or more.
 4. The high-strength steel sheet of claim 1, wherein the steel sheet has an impact toughness of 100 J or more at −40° C.
 5. A method for manufacturing of a high-strength steel sheet having excellent ductility and low-temperature toughness, comprising: heating a steel slab in a temperature range of 1100 to 1200° C., the steel slab comprising, by wt %, 0.05 to 0.12% of carbon (C), 0.2 to 0.5% of silicon (Si), 1.2 to 1.8% of manganese (Mn), 0.012% or less of phosphorus (P), 0.005% or less of sulfur (S), 0.01 to 0.06% of aluminum (Al), 0.005 to 0.02% of titanium (Ti), 0.01 to 0.03% of niobium (Nb), 0.002 to 0.006% of nitrogen (N), 0.5% or less of nickel (Ni), the balance Fe, and inevitable impurities; manufacturing the heated steel slab into a hot-rolled steel plate by rough rolling and finish rolling the heated steel slab; and cooling the hot-rolled steel plate, wherein the finish rolling is performed in a temperature range of Ar3+70° C. to Ar3+170° C. and has a thickness of 8 to 15 mm.
 6. The method of claim 5, wherein the finish rolling is performed such that a cumulative reduction ratio is 60 to 90%.
 7. The method of claim 5, wherein the cooling is air-cooled up to room temperature. 